CN101157169B - Filling soldering flux wire for titania gas coverage arc welding - Google Patents
Filling soldering flux wire for titania gas coverage arc welding Download PDFInfo
- Publication number
- CN101157169B CN101157169B CN2007101469825A CN200710146982A CN101157169B CN 101157169 B CN101157169 B CN 101157169B CN 2007101469825 A CN2007101469825 A CN 2007101469825A CN 200710146982 A CN200710146982 A CN 200710146982A CN 101157169 B CN101157169 B CN 101157169B
- Authority
- CN
- China
- Prior art keywords
- quality
- welding
- welding slag
- flux
- zro
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
- B23K35/3073—Fe as the principal constituent with Mn as next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
The invention provides a flux-cored wire for gas-shielded arc welding. The total quality of flux-cored wire which contains in its quality percentage TiO2: 6 to 12%, Al2O3: 0.4 to 0.8%, SiO2: 0.1 to 0.5%, ZrO2: 0.05 to 0.2%, Mn: 1.0 to 3.0%, Si: 0.4 to 0.9%, Al: 0.1 to 0.3% and Mg: 0.4 to 0.8%. The invention also comprises C, F, Cr, Cu, Ni, V, Nb, Ti and or Zr. The rest comprises Fe and impurities,wherein, TiO2 and Al2O3: SiO2 and ZrO2 is 10 to 20; Mg: Si and Al is 0.4 to 0.7; Na and K is 0.05 to 0.12%; and Na: K is more than 0.3. The invention has the advantages of having no molten metal falling off even the welding gap root is quite narrow along the vertical direction, having good welding performance and having excellent mechanical capacity of the welded metal.
Description
Technical field
The present invention relates to a kind ofly can be applicable to that the titanium dioxide (Titania) of the welding of carbon steel, high strength steel or low-alloy steel etc. is flux-cored wire for gas shielded arc welding for creep, particularly relate to the upward welding in the vertical position function admirable and then improved the flux-cored wire for titanic oxide gas shielded arc welding of the weld job of the welding slag fissility and the generating capacity that splashes etc. and the mechanical performance of weld metal etc.
Background technology
For the weld job that accounts for 3 one-tenth of operations, carrying out the automation of welding and the exploitation of high efficiency in the shipyard in order to promote labor savingization and high efficiency.Particularly for downward butt welding and horizontal fillet welding, be introduced into and then a lot of special-purpose welding material is developed this point from welding robot and seam welder etc., high efficiency further advances.On the other hand, mainly for middle high upward welding in the vertical position positions of usage rate such as the segmentation linkings in shipbuilding, because its suitable weld is a narrow, simultaneously structure can not reverse etc. former thereby can not advance automation, need extremely superb welding technical ability in addition again, so high efficiency and the dependence broken away from technical ability become extremely difficult.
To this, the spy opens and has proposed among the flat 8-99192 to pass through Al
2O
3, MgO, ZrO
2As neccessary composition and the mode that contains in a large number, thus the flux-cored wire (prior art 1) that can carry out the upward welding in the vertical position under the high electric current.In addition, the spy opens the operation that proposed among the 2004-34078 both to maintain in the all-position welding and weld metal performance etc., further improve upright upwards property again and the TiO 2 series arc-welding that is applicable to all-position welding with flux-cored wire (prior art 2).In addition, the spy opens and has proposed the same excellent and good flux-cored wire (prior art 3) of low-temperature flexibility weld metal of upright upwards weldability among the 2005-319508.
But hanging of motlten metal takes place apart from wide because the viscosity of welding slag and motlten metal self is not enough in the root of weld easily in the fillet welding in the vertical position that makes progress in above-mentioned prior art, and weld bead shape is also bad.This is owing to do not consider groove precision bad of the structure in the actual shipbuilding etc., and the applicable elements scope is extremely narrow to be caused.In addition, there are problem points such as the welding slag fissility is bad in the prior art 1, then have problem points such as the generating capacity that splashes is still more in the prior art 2.As mentioned above, because therefore flux-cored wire in the past can not be used in all-position welding effectively having some problems on the vertical position welding weldability to ending.
Summary of the invention
The invention that the present invention finishes in view of relevant issues point just; its purpose is to provide a kind of flux-cored wire for titanic oxide gas shielded arc welding that all-position welding is used that is suitable for; it is in upward welding in the vertical position; even under welding root gap harsh welding condition such as very wide, do not have hanging of motlten metal yet; in addition; have welding slag fissility good and the few good weld job of the generating capacity that splashes, the mechanical performance excellence of weld metal in addition.
Flux-cored wire for titanic oxide gas shielded arc welding of the present invention is a filling flux and constituting in carbon steel or alloy steel crust, in crust and solder flux totally, contains based on the welding wire gross mass:
TiO
2: 6~12 quality %,
Al
2O
3: 0.4~0.8 quality %,
SiO
2: 0.1~0.5 quality %,
ZrO
2: 0.05~0.20 quality %,
Mn:1.0~3.0 quality %,
Si:0.4~0.9 quality %,
Al:0.1~0.3 quality %,
Mg:0.4~0.8 quality %,
Surplus is Fe and unavoidable impurities, and satisfies:
(TiO
2+Al
2O
3)/(SiO
2+ZrO
2):10~20,
Mg/ (Si+Al): 0.4~0.7 (when Mg and Si and Al exist with the form of alloy, being converted into the content of Mg and Si and Al),
Na+K:0.05~0.12 quality % (when Na and K exist with the form of compound or alloy, being converted into the content of Na and K),
Na/K:0.3 above below 0.67 (when Na and K exist with the form of compound or alloy, being converted into the content of Na and K).
Flux-cored wire for titanic oxide gas shielded arc welding of the present invention is a filling flux and constituting in carbon steel or alloy steel crust, in crust and solder flux totally, contains based on the welding wire gross mass:
TiO
2: 6~12 quality %,
Al
2O
3: 0.4~0.8 quality %,
SiO
2: 0.1~0.5 quality %,
ZrO
2: 0.05~0.20 quality %,
Mn:1.0~3.0 quality %,
Si:0.4~0.9 quality %,
Al:0.1~0.3 quality %,
Mg:0.4~0.8 quality %,
C:0.01~0.12 quality %,
F:0.05~0.10 quality %,
Also contain from Cr:0.01~0.1 quality %, Cu:0.01~0.1 quality %, Ni:0.01~0.1 quality %, V:0.005~0.1 quality %, Nb:0.005~0.1 quality %, Ti:0.01~0.1 quality % and Zr:0.01~0.1 quality %, select at least a
Surplus is Fe and unavoidable impurities, and satisfies:
(TiO
2+Al
2O
3)/(SiO
2+ZrO
2):10~20,
Mg/ (Si+Al): 0.4~0.7 (when Mg and Si and Al exist with the form of alloy, being converted into the content of Mg and Si and Al),
Na+K:0.05~0.12 quality % (when Na and K exist with the form of compound or alloy, being converted into the content of Na and K),
Na/K:0.3 above below 0.67 (when Na and K exist with the form of compound or alloy, being converted into the content of Na and K).
According to the present invention, in upright upwards weldering, even under welding root gap harsh welding condition such as very wide, can access does not have hanging of motlten metal yet, in addition, and the good and few good weld job of the generating capacity that splashes of welding slag fissility.Thus, the flux-cored wire for gas shielded arc welding for creep of all-position welding can be obtained being applicable to according to the present invention, the good weld metal of mechanical performance can also be obtained.
The specific embodiment
Below, explain for flux-cored wire for gas shielded arc welding for creep of the present invention.At first, present inventor etc. are in order both to improve the welding slag fissility, prevent to become the hanging of motlten metal of the bad reason of weld bead shape simultaneously, to changing the composition of the welding slag that generally carries out, study with the method for the freezing point that improves welding slag.
In order to become the high-melting-point welding slag, open as described in the flat 8-99192 Al as the spy
2O
3MgOZrO
2Though effective, but Al
2O
3MgO has the effect that makes welding slag fissility deterioration, in addition, and ZrO
2Has the effect that increases the generating capacity that splashes.Therefore, as being used for not making the welding slag fissility and the generating capacity deterioration of splashing, and prevent that weld bead shape is bad and method that take has: (1) generates the high-melting-point welding slag, and increases the TiO that can not make welding slag fissility deterioration
2Addition; (2) in the scope that can not make welding slag fissility deterioration, add the Al that generates the high-melting-point welding slag
2O
3(3) inhibition is guaranteed arc stability but the SiO of generation low melting point welding slag
2Addition; (4) realization generates the high-melting-point welding slag but has the ZrO that increases this shortcoming of generating capacity of splashing concurrently
2The inhibition of addition, adjust these TiO respectively
2, Al
2O
3, SiO
2, ZrO
2Found that of content, adjust TiO
2And Al
2O
3Total content to SiO
2And ZrO
2The ratio of total content more effective.
In addition, except solidifying of welding slag shifted to an earlier date, also needing was composition and the characteristic that hanging of motlten metal self is difficult to take place, and generally effectively reduced the oxygen amount in the motlten metal for this reason, increased motlten metal viscosity at high temperature.Record as deoxidier Al, Si among the Te Kaiping 8-99192 more effective, but Al can generate Al according to addition
2O
3, make the fissility deterioration of welding slag thus, and make the toughness deterioration of weld metal.In addition, according to the addition of Si, can cause because of SiO
2Generation causes the reduction of welding slag freezing point, the increase of weld metal intensity and the deterioration of toughness.In the present invention as can be seen, as not bringing harmful effect can not for intensity, the toughness of weld metal, and the strong deoxidier that the oxygen amount in the motlten metal is reduced, Mg is effective, and the content of adjusting Mg is effective with respect to the ratio of the total content of Al and Si.
In addition, in order to eliminate hanging of motlten metal, the vibrations that suppress the molten bath are also effective, also can find out from the splash viewpoint of generating capacity of reduction in addition, adjustment adds up to the content ratio of Na of content and K content effective with respect to the alkali metal of Na that can improve arc stability and K (when Na, K exist with compound or alloy, being converted into the content of Na and K respectively).
Below, about the composition of flux-cored wire of the present invention, describe with regard to its composition interpolation reason and composition qualification reason.But, the content of these each compositions is the content with respect to the welding wire gross mass.In addition, the composition of this welding wire is the composition that comprises ingredient in whole formation things of solder flux and crust.
" TiO
2: 6~12 quality % "
TiO
2Play a role as welding slag formation agent and arc stabilizer.TiO
2Be lower than the welding slag amount that 6 quality % just can not guarantee only to support motlten metal, cause motlten metal to hang.In addition, if TiO
2Surpass 12 quality % then the welding slag growing amount slag inclusion too much and easily takes place.
" Al
2O
3: 0.4~0.8 quality % "
Al
2O
3Has the effect that the welding slag freezing point is risen.Al
2O
3Be lower than then this effect not of 0.4 quality %; If Al
2O
3Surpass then welding slag fissility deterioration of 0.8 quality %.
" SiO
2: 0.1~0.5 quality % "
SiO
2Effect with welding slag formation agent and arc stabilizer.SiO
2Electric arc instability when being lower than 0.1 quality %, what splash increases, if SiO
2Surpass the then freezing point decline of welding slag of 0.5 quality %, cause motlten metal to hang.
" ZrO
2: 0.05~0.20 quality % "
ZrO
2Has the effect that makes the welding slag freezing point rise and improve the fissility of welding slag.ZrO
2When being lower than 0.05 quality %, cause the fissility deterioration of welding slag by the scorification of welding slag; If ZrO
2Above increasing that 0.20 quality % then splashes.
" Mn:1.0~3.0 quality % "
Mn is when working as deoxidier, also has the intensity that improves weld metal and the effect of toughness.When Mn is lower than 1.5 quality %, because the deoxidation deficiency, reduces weld defects such as the hanging of the motlten metal that causes, pore by viscosity intensity and toughness deterioration take place.If Mn surpasses 3 quality % then the intensity of weld metal is too high.Being more preferably Mn is 1.55~2.05 quality %.This Mn can add with metal M n or ferroalloy etc. (Fe-Mn, Fe-Si-Mn etc.) form.
" Si:0.4~0.9 quality % "
Si is as the deoxidier effect time, also has the intensity that improves weld metal and the effect of toughness.When Si is lower than 0.4 quality %, take place because the viscosity that the deoxidation deficiency causes reduces weld defect, intensity and toughness deteriorations such as the hanging of the motlten metal that causes, pore.The intensity of weld metal uprises if Si surpasses 0.9 quality %, and toughness reduces simultaneously.This Si amount is the scaled value of the Si that contains in metal Si or the ferroalloy etc. (Fe-Si, Fe-Si-Mn, Ca-Si etc.).
" Al:0.1~0.3 quality % "
Al works as deoxidier and welding slag formation agent.When Al was lower than 0.1 quality %, hanging of motlten metal taken place easily.If Al surpasses the fissility deterioration of 0.3 quality % with regard to welding slag, and the toughness of weld metal reduces.Being more preferably Al is 0.2~0.3 quality %.This Al amount is the scaled value of the Al that contains in metal A l or the ferroalloy (Fe-Al).
" Mg:0.4~0.8 quality % "
Mg works as strong deoxidier.When Mg is lower than 0.4 quality %, take place because the hanging of the motlten metal that the not enough viscosity reduction that causes of deoxidation causes, and the toughness deterioration of weld metal.As MgO excessive increase in the fusion welding slag of deoxidation product, the amount of hanging of motlten metal and the generating capacity that splashes also increase if Mg surpasses 0.8 quality %.This Mg is the scaled value of the Mg that contains in metal M g or the various alloy (Al-Mg, Ni-Mg).
" C:0.01~0.12 quality % "
Therefore C can add owing to have the intensity of raising weld metal and the effect of toughness.When adding C, its content is decided to be 0.01~0.12 quality %, is preferably 0.03~0.10 quality %.It is excessive that C adds, and then the intensity of weld metal excessively rises, anti-crackle deterioration.
" F:0.05~0.10 quality % "
F prevents the generation of welding bead and air drain owing to promote to invade the discharge of the hydrogen in the molten bath, therefore can add.When adding F, be decided to be 0.05~0.10 quality %.It is excessive that F adds, and then causes the increase of splashing.
" that selects from Cr:0.01~0.1 quality %, Cu:0.01~0.1 quality %, Ni:0.01~0.1 quality %, V:0.005~0.1 quality %, Nb:0.005~0.1 quality %, Ti:0.01~0.1 quality % and Zr:0.01~0.1 quality % is at least a "
Cr, Cu, Ni, V, Nb, Ti and Zr help the intensity of weld metal to improve as alloying component, help the improvement of corrosion resistance.In order to bring into play this effect, need contain in these elements at least aly, and the situation of Cr, Cu, Ni, Ti and Zr is more than the 0.01 quality %, the situation of V, Nb is more than the 0.005 quality %.But owing to cause that because of the interpolation of Cr, Cu, Ni, V, Nb, Ti and Zr is excessive the intensity of weld metal excessively rises, the corrosion resistance deterioration, so these compositions all are decided to be below the 0.1 quality %.Comprise above-mentioned C, F, Cr, Cu, Ni, V, Nb, Ti and Zr can contain, and also can not contain.
“x=(TiO
2+Al
2O
3)/(SiO
2+ZrO
2):10~20”
Even TiO
2, Al
2O
3, SiO
2, ZrO
2Respectively in described scope, if TiO
2And Al
2O
3Total content with respect to SiO
2And ZrO
2The ratio x of total content be lower than 10, then the flowability of welding slag increases, and can not support motlten metal.On the other hand, ratio x surpasses at 20 o'clock, and the scorification of welding slag increases, the fissility deterioration of welding slag.In a word, by generating the SiO of low melting point welding slag
2With the splash ZrO of generating capacity of increase
2Total content be made as denominator, generate the TiO of high-melting-point welding slag
2And Al
2O
3Total content its ratio x of being made as the branch period of the day from 11 p.m. to 1 a.m in 10~20 suitable scope, adjust, thereby can not make the welding slag fissility and the generating capacity deterioration of splashing, can realize the upright upwards raising of property.The more preferably scope of x is 12~19.
" y=Mg/ (Si+Al): 0.4~0.7 (when Mg and Si and Al exist with the form of alloy, being converted into the content of Mg and Si and Al) "
Even in described scope, Mg is lower than at 0.4 o'clock with respect to the ratio y of the total content of Si and Al to the content of Mg, Al, Si respectively, the intensity of weld metal increases, and toughness descends.Y surpasses at 0.7 o'clock, and the generation that motlten metal hangs, splashes will increase.In a word, though by being made as denominator at the Si of the degraded in mechanical properties that effectively still makes weld metal aspect the upright upwards property and the total content of Al, to improve the viscosity of motlten metal and improve the Mg of particularly toughness of weld metal by its very strong deoxidizing capacity and the ratio y that content is made as the branch period of the day from 11 p.m. to 1 a.m is adjusted in 0.4~0.7 suitable scope, thereby can not make the degraded in mechanical properties of weld metal, can realize the upright upwards raising of property.The more preferably scope of y is 0.4~0.6.
" Na+K:0.05~0.12 quality %, Na/K:0.3 above (Na, K are converted into the content of Na, K respectively when existing with compound or alloy) "
Na and K have the effect of arc stabilizer, can prevent hanging of motlten metal by the vibration that suppresses the molten bath.The total content of Na and K is lower than 0.05 quality % then can not obtain described effect, if the total content of Na and K surpasses 0.12 quality %, then takes place easily to generate hanging of the motlten metal that too much causes by the low melting point welding slag.In addition, Na content is lower than at 0.3 o'clock with respect to the ratio of K content, the arc stability deterioration, and the generating capacity that splashes increases, and hanging of motlten metal taken place in addition easily.
Also have, the alloying element of Si, Mn etc. can add from crust and/or solder flux.In addition, for improving corrosion resistance, high strength and the high-temperature corrosion resistance etc. of weld part, can add above-mentioned alloying component (Cr, Cu, Ni, V, Nb etc.) in addition.In addition, can also add fluoride.
In addition, not restriction of the filling shape of the solder flux in the state of welding wire surface and welding wire cross section.Also have, as the composition beyond above-mentioned, the Fe as the constituent of ferroalloy such as crust, Fe-Mn, Fe-Si and iron powder etc. is arranged, surplus is a unavoidable impurities.As unavoidable impurities P, S, Sb, As, Pb etc. are arranged, these unavoidable impurities need be restricted to below the 0.1 quality % in total amount.
[embodiment]
Below, for the effect of the embodiment of the invention, compare with the comparative example that breaks away from the scope of the invention and describe.The example of the raw material of each composition of defined among following table 1 expression the present invention.The raw material of expression in this table 1 is suitably cooperated, be filled in steel (JIS G 23 3141, the SPCC) crust, making solder flux is 15 quality % with respect to the ratio of welding wire gross mass, makes the flux-cored wire of gage of wire 1.2mm.The assay value of the flux-cored wire component content of expression embodiment and comparative example in table 2 and the table 3.The principal component of the surplus beyond the composition in table 2 and the table 3 is Fe, contains P, S, N, Cu etc. as inevitable impurity.
[table 1]
TiO 2 | Rutile, Le コ キ シ Application (mineral products name), high titanium slag etc. |
Al 2O 3 | Aluminium oxide etc. |
TiO 2 | Rutile, Le コ キ シ Application (mineral products name), high titanium slag etc. |
ZrO 2 | Zirconia, zircon sand etc. |
SiO 2 | Silica sand etc. |
Si | Fe-Si alloy, Fe-Si-Mn alloy etc. |
Mn | Fe-Mn alloy, Fe-Si-Mn alloy, metal M n etc. |
Al | Metal A l, Al-Mn alloy, Fe-Al alloy, aluminium oxide etc. |
Mg | Metal M g, Al-Mg alloy, Ni-Mg alloy, magnesia etc. |
Na | Fluoridize soda, ice crystal, albite, silicic acid metatitanic acid soda-lime glass, silicic acid metatitanic acid soda potash glass etc. |
K | Potassium fluosilicate, potassic feldspar, silicic acid metatitanic acid potash glass, silicic acid metatitanic acid soda potash glass etc. |
[table 2-1]
[table 2-2]
[table 2-3]
[table 3-1]
[table 3-2]
[table 3-3]
Use the comparative example 1~22 of expression in above-mentioned table 2 and the table 3 and the flux-cored wire of embodiment 1~15; use the steel plate of JIS G 3106, SM490A as soldered material; as protective gas with the CO2 of 100 quality % with 25 liters of/minute supplies of flow; implement each soldering test of following (1)~(3), estimate for its weldability.
(1) the upright upwards evaluation of weldering property
In the method for following table 4 expression, stand the welding bead droop test in the upwards weldering, estimated upright upwards weldering property.
[table 4]
The welding position | Upwards upright |
For the examination steel plate | T type fillet weld test plate (steel grade SM490A, thickness of slab 12mm, length 400mm) |
The root gap of weld | 6mm |
Welding current | 300A |
Arc voltage | 30V |
Speed of welding | 8~14cm/ branch |
(2) evaluation of weld job and welding slag fissility
The evaluation of weld job is undertaken by upright upwards fillet welding, estimates for the functional evaluation and the welding slag fissility of the generating capacity that splashes.Evaluation criterion is as follows.
(2-1) evaluation of weld job
(generating capacity splashes: be lower than 1.5g/ minute) that the generating capacity that splashes is few: zero
Generating capacity many slightly (generating capacity splashes: more than 1.5g/ minute) splashes: *
(2-2) evaluation of welding slag fissility
(welding slag is peeled off rate (=welding slag nature strip length/welding is long) naturally: more than 25%) that the welding slag fissility is good: zero
(welding slag is peeled off rate (=welding slag nature strip length/welding is long) naturally: be lower than 25%) that the welding slag fissility is bad: *
(3) use the confession examination steel plate that meets JI S G 3106 (SM490A),, weld with the test method of following table 5 expression according to the metallized test method of fine melt about defined among the JIS Z 3313.
Evaluation criterion is as follows.
Absorption that pendulum impact test causes can be for more than the 60J but be lower than 90J: zero
The absorption that pendulum impact test causes can be lower than 60J's: *
The evaluation result of each above-mentioned soldering test is represented with table 6 and table 7.
[table 5]
[table 6]
[table 7]
Shown in this table 6 and table 7, comparative example 1 is because TiO
2Exceeded its lower limit, and only upright upwards property is poor, comparative example 2 is because TiO only
2Therefore exceeded its higher limit, taken place to form increase that sagging, the big grain of the motlten metal that dosage too much causes splashes, reach bad and the deterioration mechanical performance that causes by deoxidation by welding slag.Comparative example 3 is because Al only
2O
3Therefore exceeded its lower limit, reduced by the viscosity of welding slag and the upright upwards property that causes is poor, comparative example 4 is because Al only
2O
3Therefore exceeded its higher limit, the bad of the welding slag fissility that caused by the welding slag scorification on weld metal taken place.Comparative example 5 is because SiO
2Exceed its lower limit, and (TiO
2+ Al
2O
3)/(SiO
2+ ZrO
2) ratio x also exceed its higher limit, therefore solidify too fast, opposite as seen interference the and the upright upwards deterioration of property that causes by welding slag.Comparative example 6 is because SiO only
2Exceeded its higher limit, thus welding slag solidified late, welding slag can not keep motlten metal, and the sagging of motlten metal taken place.
Comparative example 7 is because ZrO only
2Therefore exceeded its lower limit, the bad of the welding slag fissility that caused by the welding slag scorification on weld metal taken place.Comparative example 8 is because ZrO only
2Exceeded its higher limit, thus welding slag solidify slowly, the sagging of motlten metal taken place.In the comparative example 9, TiO
2, Al
2O
3, SiO
2, ZrO
2In its prescribed limit, has only (TiO
2+ Al
2O
3)/(SiO
2+ ZrO
2) ratio x exceed its lower limit, so welding slag solidify slowly, and the sagging of motlten metal taken place.In the comparative example 10, TiO
2, Al
2O
3, SiO
2, ZrO
2In its prescribed limit, has only (TiO
2+ Al
2O
3)/(SiO
2+ ZrO
2) ratio x exceed its higher limit, so welding slag solidify too fast, opposite as seen interference the and the upright upwards deterioration of property that causes, and the welding slag scorification on weld metal has taken place and the welding slag fissility that causes bad by welding slag.
Comparative example 11 since only Mn exceeded its higher limit, thereby the Mn of weld metal amount too much, hot strength is low.In addition, the upright deterioration that as seen comparative example 11 is caused by excessive generation low-melting compound Mn in the welding slag to enterprising property, and splashing of big grain also taken place.Comparative example 12 since only Mn exceeded its lower limit, so deoxidizing capacity is poor, the impact property of weld metal is poor, and has taken place bad by deoxidation and weld defect that cause.Comparative example 13 since only Si exceeded its lower limit, so deoxidizing capacity is poor, the impact property of weld metal is poor.In addition, comparative example 13 is that the centrality of electric arc strengthens, upright example to enterprising property deterioration.Comparative example 14 since only Si exceeded its higher limit, so the Si of weld metal amount is too much, the visible and deterioration of the impact property that cause too high by hot strength.
Comparative example 15 since only Al exceeded its lower limit, therefore as seen descend and the upright upwards deterioration of property that causes by the viscosity of motlten metal.Comparative example 16 since only Al exceeded its higher limit, so impact property variation of weld metal, and as seen by excessive generation Al in the welding slag
2O
3And the deterioration of the welding slag fissility that causes.Comparative example 17 since only Mg exceeded its lower limit, so deoxidizing capacity is poor, the impact property of weld metal is poor, and is as seen descended by the viscosity of motlten metal and the upright upwards deterioration of property that causes.Comparative example 18 since only Mg exceeded its higher limit, therefore cross strong and Mn and the utilization rate of Si in weld metal that cause are too high, the deterioration of the visible too high impact property that causes of hot strength by deoxidizing capacity.In addition, the welding slag of big grain increases, and the deterioration of the welding slag fissility that excessive generation MnO causes in the visible welding slag.
Comparative example 19 its Si, Al, Mg are in prescribed limit, and the ratio y of Mg/ (Si+Al) exceeds its lower limit, and the hot strength of therefore visible weld metal excessively increases the deterioration of the impact property that causes.The Si of comparative example 20, Al, Mg are in its prescribed limit, and the ratio y of Mg/ (Si+Al) exceeds its higher limit, the upright upwards deterioration of property that the viscosity deficiency of therefore visible motlten metal causes.Comparative example 21 is because Na+K exceeds its lower limit, so the electric arc centrality strengthens, upright upwards property deterioration, and big grain has taken place splash.Comparative example 22 is because Na+K exceeds its higher limit, so visible low-melting compound Na
2O and K
2The upright upwards deterioration of property that the excessive generation of O causes.Comparative example 23 since Na+K in its prescribed limit and Na+K has exceeded its lower limit, the therefore increase of splashing of big grain.
To this, any satisfies the prescribed limit of the invention described above embodiment 1~15, and therefore above-mentioned whole welding characteristics are good.
Moreover, for the weld job that reaches horizontal fillet welding downwards, confirm by same test that also any is all good for embodiments of the invention.
As previously discussed, according to the present invention, can deterioration the do not splash weld job of generating capacity, welding slag fissility etc. and the mechanical performance of weld metal are even also can prevent hanging of motlten metal and welding slag under the welding condition of being put the high welding current that causes and very wide harshnesses such as root of weld interval by upright upwards welding position.
Claims (2)
1. flux-cored wire for titanic oxide gas shielded arc welding, it is that filling flux forms in carbon steel or alloy steel crust, it is characterized in that, in crust and solder flux totally, contains based on the welding wire gross mass:
TiO
2: 6~12 quality %,
Al
2O
3: 0.4~0.8 quality %,
SiO
2: 0.1~0.5 quality %,
ZrO
2: 0.05~0.20 quality %,
Mn:1.0~3.0 quality %,
Si:0.4~0.9 quality %,
Al:0.1~0.3 quality %,
Mg:0.4~0.8 quality %,
Surplus is Fe and unavoidable impurities, and satisfies:
(TiO
2+Al
2O
3)/(SiO
2+ZrO
2):10~20,
Mg/(Si+Al):0.4~0.7,
Wherein, when Mg and Si and Al exist with alloy morphology, be the content that is converted into Mg and Si and Al,
Na+K:0.05~0.12 quality %,
Na/K:0.3 is above below 0.67,
Wherein, when Na and K exist with the form of compound or alloy, be the content that is converted into Na and K.
2. flux-cored wire for titanic oxide gas shielded arc welding, it is that filling flux forms in carbon steel or alloy steel crust, it is characterized in that, in crust and solder flux totally, contains based on the welding wire gross mass:
TiO
2: 6~12 quality %,
Al
2O
3: 0.4~0.8 quality %,
SiO
2: 0.1~0.5 quality %,
ZrO
2: 0.05~0.20 quality %,
Mn:1.0~3.0 quality %,
Si:0.4~0.9 quality %,
Al:0.1~0.3 quality %,
Mg:0.4~0.8 quality %,
C:0.01~0.12 quality %,
F:0.05~0.10 quality %,
Also contain from Cr:0.01~0.1 quality %, Cu:0.01~0.1 quality %, Ni:0.01~0.1 quality %, V:0.005~0.1 quality %, Nb:0.005~0.1 quality %, Ti:0.01~0.1 quality % and Zr:0.01~0.1 quality %, select at least a
Surplus is Fe and unavoidable impurities, and satisfies:
(TiO
2+Al
2O
3)/(SiO
2+ZrO
2):10~20,
Mg/(Si+Al):0.4~0.7,
Wherein, when Mg and Si and Al exist with alloy morphology, be the content that is converted into Mg and Si and Al,
Na+K:0.05~0.12 quality %,
Na/K:0.3 is above below 0.67,
Wherein, when Na and K exist with the form of compound or alloy, be the content that is converted into Na and K.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2006-271316 | 2006-10-02 | ||
JP2006271316A JP4986562B2 (en) | 2006-10-02 | 2006-10-02 | Flux-cored wire for titania-based gas shielded arc welding |
JP2006271316 | 2006-10-02 |
Publications (2)
Publication Number | Publication Date |
---|---|
CN101157169A CN101157169A (en) | 2008-04-09 |
CN101157169B true CN101157169B (en) | 2010-06-02 |
Family
ID=39305469
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN2007101469825A Active CN101157169B (en) | 2006-10-02 | 2007-09-03 | Filling soldering flux wire for titania gas coverage arc welding |
Country Status (3)
Country | Link |
---|---|
JP (1) | JP4986562B2 (en) |
KR (1) | KR100920550B1 (en) |
CN (1) | CN101157169B (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN106001985A (en) * | 2015-03-30 | 2016-10-12 | 株式会社神户制钢所 | Flux cored wire for gas shielded arc welding |
CN106001986A (en) * | 2015-03-30 | 2016-10-12 | 株式会社神户制钢所 | Flux cored wire for gas shielded arc welding |
Families Citing this family (24)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5283993B2 (en) * | 2008-07-09 | 2013-09-04 | 株式会社神戸製鋼所 | Flux-cored wire for titania-based gas shielded arc welding |
KR101046136B1 (en) * | 2008-12-24 | 2011-07-01 | 주식회사 포스코 | Flux cored wire for gas shielded arc welding |
JP5351641B2 (en) * | 2009-07-23 | 2013-11-27 | 株式会社神戸製鋼所 | Flux cored wire |
JP5415998B2 (en) * | 2010-03-11 | 2014-02-12 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding |
JP5450260B2 (en) * | 2010-05-27 | 2014-03-26 | 株式会社神戸製鋼所 | Weld metal with excellent hot crack resistance |
JP5669624B2 (en) * | 2010-08-10 | 2015-02-12 | 株式会社神戸製鋼所 | Titanium oxide raw material for welding material, welding material using the same, and method for producing titanium oxide raw material for welding material |
JP5242665B2 (en) * | 2010-12-08 | 2013-07-24 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
JP5518773B2 (en) * | 2011-03-15 | 2014-06-11 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
CN102179640B (en) * | 2011-04-26 | 2013-03-13 | 武汉铁锚焊接材料股份有限公司 | High-strength and high-toughness metal powder flux-cored wire |
JP5863570B2 (en) * | 2012-06-08 | 2016-02-16 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
CN102873468B (en) * | 2012-09-18 | 2014-10-01 | 武汉铁锚焊接材料股份有限公司 | High-speed flat fillet weld flux-cored wire and preparation and application thereof |
JP5845168B2 (en) * | 2012-12-28 | 2016-01-20 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding and gas shielded arc welding method |
JP6085205B2 (en) * | 2013-03-25 | 2017-02-22 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding |
JP6040133B2 (en) * | 2013-10-03 | 2016-12-07 | 株式会社神戸製鋼所 | Gas shield arc welding method |
CN104117789B (en) * | 2014-08-06 | 2016-05-25 | 武汉铁锚焊接材料股份有限公司 | A kind of low-temperature steel flux-cored wire |
JP6322096B2 (en) * | 2014-09-09 | 2018-05-09 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
CN105057916A (en) * | 2015-07-30 | 2015-11-18 | 洛阳双瑞特种合金材料有限公司 | Stainless steel flux-cored wire capable of receiving postweld heat treatment |
CN105081609A (en) * | 2015-09-22 | 2015-11-25 | 机械科学研究院哈尔滨焊接研究所 | High-strength and high-toughness all-position-welding gas shield flux-cored wire for weather-resistant steel |
JP6719217B2 (en) * | 2016-01-25 | 2020-07-08 | 株式会社神戸製鋼所 | Stainless steel flux cored wire |
CN106041360A (en) * | 2016-07-27 | 2016-10-26 | 天津大桥金属焊丝有限公司 | Vertical position fillet welding small fillet titanium type high-toughness flux-cored wire and manufacturing method thereof |
CN106312370B (en) * | 2016-10-28 | 2018-10-12 | 北京工业大学 | A kind of 308L stainless flux-cored wires for plate sheet welding |
CN110315240A (en) * | 2018-03-29 | 2019-10-11 | 株式会社神户制钢所 | Flux-cored wire |
EP3778111A4 (en) * | 2018-03-29 | 2022-01-19 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Flux-cored wire |
CN113458649B (en) * | 2021-07-09 | 2022-12-06 | 昆山京群焊材科技有限公司 | Self-protection flux-cored wire containing titanium carbide particles |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1381060A (en) * | 2000-03-30 | 2002-11-20 | Abb股份有限公司 | Induction winding |
CN1387975A (en) * | 2001-05-28 | 2003-01-01 | 基斯韦尔株式会社 | Welding wire of filling flux of gas protection electric arc welding using for high-strength steel |
CN1597236A (en) * | 2003-09-16 | 2005-03-23 | 株式会社神户制钢所 | Metal wire of filling titanium dioxide flux |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60213398A (en) * | 1984-04-06 | 1985-10-25 | Nippon Steel Corp | Low-hydrogen type coated arc welding electrode |
JPS61286089A (en) * | 1985-06-11 | 1986-12-16 | Daido Steel Co Ltd | Gas shielded arc welding method |
JPS6233094A (en) * | 1985-07-31 | 1987-02-13 | Daido Steel Co Ltd | Flux cored wire for welding |
JPS6234697A (en) * | 1985-08-09 | 1987-02-14 | Daido Steel Co Ltd | Flux cored wide for welding |
JP2711077B2 (en) * | 1994-09-29 | 1998-02-10 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding |
JP3730440B2 (en) | 1999-04-23 | 2006-01-05 | 日鐵住金溶接工業株式会社 | Flux-cored wire for gas shielded arc welding |
KR100355581B1 (en) | 2000-09-23 | 2002-10-11 | 고려용접봉 주식회사 | Flux cored wire for gas shield arc welding |
JP3758040B2 (en) * | 2002-07-26 | 2006-03-22 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding for low alloy heat resistant steel |
JP4259887B2 (en) * | 2003-01-31 | 2009-04-30 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding for corrosion resistant steel |
-
2006
- 2006-10-02 JP JP2006271316A patent/JP4986562B2/en active Active
-
2007
- 2007-09-03 CN CN2007101469825A patent/CN101157169B/en active Active
- 2007-10-01 KR KR1020070098723A patent/KR100920550B1/en active IP Right Grant
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1381060A (en) * | 2000-03-30 | 2002-11-20 | Abb股份有限公司 | Induction winding |
CN1387975A (en) * | 2001-05-28 | 2003-01-01 | 基斯韦尔株式会社 | Welding wire of filling flux of gas protection electric arc welding using for high-strength steel |
CN1597236A (en) * | 2003-09-16 | 2005-03-23 | 株式会社神户制钢所 | Metal wire of filling titanium dioxide flux |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN106001985A (en) * | 2015-03-30 | 2016-10-12 | 株式会社神户制钢所 | Flux cored wire for gas shielded arc welding |
CN106001986A (en) * | 2015-03-30 | 2016-10-12 | 株式会社神户制钢所 | Flux cored wire for gas shielded arc welding |
CN106001986B (en) * | 2015-03-30 | 2019-06-21 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
CN106001985B (en) * | 2015-03-30 | 2019-06-21 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
Also Published As
Publication number | Publication date |
---|---|
JP4986562B2 (en) | 2012-07-25 |
KR100920550B1 (en) | 2009-10-08 |
JP2008087044A (en) | 2008-04-17 |
CN101157169A (en) | 2008-04-09 |
KR20080030935A (en) | 2008-04-07 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN101157169B (en) | Filling soldering flux wire for titania gas coverage arc welding | |
US10286499B2 (en) | Ni based alloy flux cored wire | |
CN101380706B (en) | Flux-cored wire for gas-shielded arc welding | |
KR100805494B1 (en) | Ni-BASE ALLOY FLUX-CORED WIRE | |
CN101157164B (en) | Gas coverage arc welding compound core solder wire for steel with high tension | |
JP5384312B2 (en) | Flux-cored wire for gas shielded arc welding for weathering steel | |
CN101623799B (en) | Flux-cored wire for titanic oxide gas shielded arc welding | |
CN1966199B (en) | Flux cored wire for gas protection electrical arc welding | |
JP2013151001A (en) | Flux-cored wire for gas-shielded arc welding for weather-resistant steel | |
JP2014113615A (en) | Flux-cored wire for carbon dioxide gas shielded arc welding | |
CN105081603A (en) | Ni BASED ALLOY FLUX CORED WIRE | |
KR100985681B1 (en) | Flux-cored wire for gas shielded arc welding | |
CN101623802B (en) | Flux-cored wire | |
JP2614969B2 (en) | Gas shielded arc welding titania-based flux cored wire | |
US20220016734A1 (en) | Ni-BASED ALLOY FLUX-CORED WIRE | |
JP4259887B2 (en) | Flux-cored wire for gas shielded arc welding for corrosion resistant steel | |
JP2711077B2 (en) | Flux-cored wire for gas shielded arc welding | |
JP7321958B2 (en) | Flux-cored wire for gas-shielded arc welding of seawater-resistant steel | |
JP2020015092A (en) | Flux-cored wire for welding two-phase stainless steel, welding method and weld metal | |
JP2019171473A (en) | Flux-cored wire | |
JP5409132B2 (en) | Flux-cored wire for gas shielded arc welding | |
JP2020142277A (en) | FLUX-CORED WIRE FOR Ar-CO2 MIXED GAS SHIELD ARC-WELDING OF ATMOSPHERIC CORROSION RESISTANT STEEL | |
JP2021115596A (en) | Flux cored wire for welding galvanized steel sheet | |
JPH08281478A (en) | Titania flux cored wire for gas shielded arc welding | |
JPH0381094A (en) | Flux cored wire for welding stainless steel |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
C06 | Publication | ||
PB01 | Publication | ||
C10 | Entry into substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
C14 | Grant of patent or utility model | ||
GR01 | Patent grant |